KR20150075539A - Method for manufacturing ferritic stainless steel sheet with excellent formability - Google Patents
Method for manufacturing ferritic stainless steel sheet with excellent formability Download PDFInfo
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- KR20150075539A KR20150075539A KR1020130163591A KR20130163591A KR20150075539A KR 20150075539 A KR20150075539 A KR 20150075539A KR 1020130163591 A KR1020130163591 A KR 1020130163591A KR 20130163591 A KR20130163591 A KR 20130163591A KR 20150075539 A KR20150075539 A KR 20150075539A
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- rolling
- hot
- ferritic stainless
- stainless steel
- cold
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- 229910001220 stainless steel Inorganic materials 0.000 title claims abstract description 34
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 21
- 238000000034 method Methods 0.000 title claims description 16
- 238000005098 hot rolling Methods 0.000 claims abstract description 49
- 238000005097 cold rolling Methods 0.000 claims abstract description 32
- 238000000137 annealing Methods 0.000 claims abstract description 23
- 239000000463 material Substances 0.000 claims abstract description 13
- 229910000831 Steel Inorganic materials 0.000 claims abstract description 12
- 239000010959 steel Substances 0.000 claims abstract description 12
- 238000001953 recrystallisation Methods 0.000 claims abstract description 7
- 238000005096 rolling process Methods 0.000 claims description 19
- 229910052757 nitrogen Inorganic materials 0.000 claims description 7
- 229910052796 boron Inorganic materials 0.000 claims description 5
- 229910052799 carbon Inorganic materials 0.000 claims description 5
- 230000009467 reduction Effects 0.000 claims description 5
- 229910052720 vanadium Inorganic materials 0.000 claims description 5
- 229910052782 aluminium Inorganic materials 0.000 claims description 4
- 229910052726 zirconium Inorganic materials 0.000 claims description 4
- 239000013078 crystal Substances 0.000 abstract description 12
- 239000000203 mixture Substances 0.000 abstract description 4
- 239000012467 final product Substances 0.000 abstract description 3
- 230000008569 process Effects 0.000 description 10
- PXHVJJICTQNCMI-UHFFFAOYSA-N nickel Substances [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 description 8
- 239000011651 chromium Substances 0.000 description 7
- 230000007797 corrosion Effects 0.000 description 7
- 238000005260 corrosion Methods 0.000 description 7
- 230000000052 comparative effect Effects 0.000 description 6
- 239000010955 niobium Substances 0.000 description 6
- 239000010935 stainless steel Substances 0.000 description 6
- 239000010936 titanium Substances 0.000 description 6
- 239000010949 copper Substances 0.000 description 5
- 239000011572 manganese Substances 0.000 description 5
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 4
- 239000010960 cold rolled steel Substances 0.000 description 3
- 230000006866 deterioration Effects 0.000 description 3
- 229910052750 molybdenum Inorganic materials 0.000 description 3
- 229910052758 niobium Inorganic materials 0.000 description 3
- 239000002994 raw material Substances 0.000 description 3
- 238000005482 strain hardening Methods 0.000 description 3
- 229910052719 titanium Inorganic materials 0.000 description 3
- 229910000859 α-Fe Inorganic materials 0.000 description 3
- ZOKXTWBITQBERF-UHFFFAOYSA-N Molybdenum Chemical compound [Mo] ZOKXTWBITQBERF-UHFFFAOYSA-N 0.000 description 2
- QAOWNCQODCNURD-UHFFFAOYSA-N Sulfuric acid Chemical compound OS(O)(=O)=O QAOWNCQODCNURD-UHFFFAOYSA-N 0.000 description 2
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 description 2
- 238000007796 conventional method Methods 0.000 description 2
- 229910052802 copper Inorganic materials 0.000 description 2
- 238000010438 heat treatment Methods 0.000 description 2
- 230000006872 improvement Effects 0.000 description 2
- 229910052751 metal Inorganic materials 0.000 description 2
- 239000002184 metal Substances 0.000 description 2
- 239000011733 molybdenum Substances 0.000 description 2
- GUCVJGMIXFAOAE-UHFFFAOYSA-N niobium atom Chemical compound [Nb] GUCVJGMIXFAOAE-UHFFFAOYSA-N 0.000 description 2
- 230000003647 oxidation Effects 0.000 description 2
- 238000007254 oxidation reaction Methods 0.000 description 2
- 229910052698 phosphorus Inorganic materials 0.000 description 2
- 238000001556 precipitation Methods 0.000 description 2
- 229910052717 sulfur Inorganic materials 0.000 description 2
- ZOXJGFHDIHLPTG-UHFFFAOYSA-N Boron Chemical compound [B] ZOXJGFHDIHLPTG-UHFFFAOYSA-N 0.000 description 1
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 1
- ZAMOUSCENKQFHK-UHFFFAOYSA-N Chlorine atom Chemical compound [Cl] ZAMOUSCENKQFHK-UHFFFAOYSA-N 0.000 description 1
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 description 1
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 description 1
- 229910000881 Cu alloy Inorganic materials 0.000 description 1
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 description 1
- OAICVXFJPJFONN-UHFFFAOYSA-N Phosphorus Chemical compound [P] OAICVXFJPJFONN-UHFFFAOYSA-N 0.000 description 1
- XUIMIQQOPSSXEZ-UHFFFAOYSA-N Silicon Chemical compound [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 description 1
- NINIDFKCEFEMDL-UHFFFAOYSA-N Sulfur Chemical compound [S] NINIDFKCEFEMDL-UHFFFAOYSA-N 0.000 description 1
- ATJFFYVFTNAWJD-UHFFFAOYSA-N Tin Chemical compound [Sn] ATJFFYVFTNAWJD-UHFFFAOYSA-N 0.000 description 1
- 230000002411 adverse Effects 0.000 description 1
- 229910045601 alloy Inorganic materials 0.000 description 1
- 239000000956 alloy Substances 0.000 description 1
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 1
- 230000008901 benefit Effects 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 238000005266 casting Methods 0.000 description 1
- 230000008859 change Effects 0.000 description 1
- 239000000460 chlorine Substances 0.000 description 1
- 229910052801 chlorine Inorganic materials 0.000 description 1
- 229910052804 chromium Inorganic materials 0.000 description 1
- 238000002425 crystallisation Methods 0.000 description 1
- 230000008025 crystallization Effects 0.000 description 1
- 230000007547 defect Effects 0.000 description 1
- 230000008570 general process Effects 0.000 description 1
- 229910000765 intermetallic Inorganic materials 0.000 description 1
- 229910052748 manganese Inorganic materials 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 238000012986 modification Methods 0.000 description 1
- 230000004048 modification Effects 0.000 description 1
- 229910052759 nickel Inorganic materials 0.000 description 1
- 239000011574 phosphorus Substances 0.000 description 1
- 239000002244 precipitate Substances 0.000 description 1
- 239000000047 product Substances 0.000 description 1
- 238000005204 segregation Methods 0.000 description 1
- VSZWPYCFIRKVQL-UHFFFAOYSA-N selanylidenegallium;selenium Chemical compound [Se].[Se]=[Ga].[Se]=[Ga] VSZWPYCFIRKVQL-UHFFFAOYSA-N 0.000 description 1
- 229910052710 silicon Inorganic materials 0.000 description 1
- 239000010703 silicon Substances 0.000 description 1
- 230000000087 stabilizing effect Effects 0.000 description 1
- 239000011593 sulfur Substances 0.000 description 1
- GPPXJZIENCGNKB-UHFFFAOYSA-N vanadium Chemical compound [V]#[V] GPPXJZIENCGNKB-UHFFFAOYSA-N 0.000 description 1
Images
Classifications
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B3/00—Rolling materials of special alloys so far as the composition of the alloy requires or permits special rolling methods or sequences ; Rolling of aluminium, copper, zinc or other non-ferrous metals
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Heat Treatment Of Sheet Steel (AREA)
Abstract
The present invention relates to a method of manufacturing a ferritic stainless steel having excellent formability that improves moldability of a final product by breaking coarse crystal grains having a rotate-cube orientation, A method of manufacturing a ferritic stainless steel excellent in moldability includes the steps of: preparing molten steel whose composition is adjusted for producing ferritic stainless steel as a slab; Hot rolling the prepared slab; Hot-rolling the hot-rolled plate at a temperature below the recrystallization temperature of the plate; Hot rolling the hot rolled plate; Cold-rolling the hot-rolled sheet material; And cold rolling annealing the cold-rolled plate.
Description
The present invention relates to a method for producing a ferritic stainless steel having excellent formability, and more particularly to a ferritic stainless steel having excellent formability for improving the formability of a final product by breaking coarse crystal grains having a rotate-cube orientation Ferritic stainless steel.
Ferritic stainless steels are less expensive than austenitic stainless steels, have lower thermal expansion rates, and are widely used for heaters, sink tops, facades, electrical appliances, and electronic components because of their excellent surface gloss, formability, and oxidation resistance.
Ferritic stainless steel cold rolled steel sheets are produced by hot rolling, hot rolling annealing, cold rolling and cold rolling annealing.
Hot rolling refers to rolling performed at a temperature not lower than the recrystallization temperature (½ of melting point) of the material. Generally, ferritic stainless steels are hot-rolled at 800 to 1300 ° C. Cold rolling refers to rolling performed at a temperature of room temperature. Rolling is performed by heating to a temperature not higher than the recrystallization temperature while separating it from cold rolling which is rolled without special heating, which is called hot rolling.
Generally, the ferritic stainless steels are left in the rolled plate without breakage even after the hot rolling and hot-rolling annealing process, resulting in a loss of formability. It is known that coarse grains remain because the work hardening rate is low because the conventional hot rolling is performed at a high temperature and the recrystallization fraction is also low when the work hardening rate is low.
In order to prevent such deterioration of moldability, it is known that control of manufacturing process parameters such as hot rolling, hot annealing, cold rolling and cold rolling annealing is particularly important as well as improvement of casting structure such as improvement of slab equilibrium constant.
Particularly, since coarse grains having a rotated cube aggregate texture (hereinafter referred to as RW aggregate structure) present after hot rolling represent a low r-value (ratio of plastic deformation of Lankford) It is necessary to change the manufacturing process of the hot-rolled steel and the like so that the steel sheet can be transformed into a structure having a high r-value.
On the other hand, in the past, hot rolling has been widely used as a step of complementing cold rolling.
As described in, for example, "a method of manufacturing a stainless steel cold-rolled steel sheet excellent in surface gloss (JP-A-10-2011-0071513) ", hot rolled in a first rolling pass during cold rolling, Low productivity by multi-pass rolling is solved.
However, the present applicant has pointed out that warm rolling can compensate for cold rolling, but if warm rolling is performed between hot rolling and warm rolling, it is possible to destroy RW aggregate, which is a coarse crystal that is not broken during the hot rolling process. Thereby completing the present invention.
The present invention relates to a ferrite-based ferrite-based alloy which is capable of improving the formability of a final product by performing hot rolling between hot rolling and cold rolling in order to break coarse crystal grains having a rotate-cube orientation To a method of manufacturing stainless steel.
A method of manufacturing a ferritic stainless steel excellent in moldability according to an embodiment of the present invention includes the steps of: preparing molten steel whose components have been adjusted for producing a ferritic stainless steel as a slab; Hot rolling the prepared slab; Hot-rolling the hot-rolled plate at a temperature below the recrystallization temperature of the plate; Hot rolling the hot rolled plate; Cold-rolling the hot-rolled sheet material; And cold rolling annealing the cold-rolled plate.
At this time, the warm rolling temperature in the warm rolling step is preferably 400 to 700 ° C.
In the warm rolling step, the reduction rate is preferably 10 to 50%.
The molten steel contains, by wt%, C: not more than 0.10% (excluding 0%), Si: not more than 1.0% (excluding 0%), Mn: not more than 1.0% ), S: not more than 0.020% (excluding 0%), Ni: not more than 2.0% (excluding 0%), Cr: 8.0 to 30%, N: not more than 0.05% And the like.
The molten steel preferably contains Al in an amount of not more than 0.10% (excluding 0%), Mo in an amount of not more than 1.0% (excluding 0%), Cu in an amount of not more than 1.0% (excluding 0%), Ti in an amount of 0.01 to 0.50% : 0.01 to 0.50%, V: 0.01 to 0.30%, Zr: 0.01 to 0.30%, and B: 0.0010 to 0.0100%.
According to an embodiment of the present invention, hot rolling is performed between hot rolling and cold rolling to break coarse crystal grains such as rotated cube aggregate existing in a hot rolled plate, It is possible to produce a ferritic stainless steel excellent in moldability.
FIG. 1A is a result of observing a microstructure with an inverse pole figure (IPF) map after hot-rolling a hot-rolled plate by a conventional process,
FIG. 1B is a result of observing the microstructure with an inverse pole figure (IPF) map after hot rolling the hot rolled plate by the process according to the present invention,
FIG. 2A is a result of observing a microstructure with an inverse pole figure (IPF) map after cold rolling and cold rolling annealing of a hot rolled plate by a conventional process,
FIG. 2B is a result of observing the microstructure with an inverse pole figure (IPF) map after cold rolling and cold rolling annealing the hot rolled plate by the process according to the present invention.
Hereinafter, embodiments of the present invention will be described in detail with reference to the accompanying drawings. It will be apparent to those skilled in the art that the present invention may be embodied in many different forms and should not be construed as limited to the embodiments set forth herein. Rather, these embodiments are provided so that this disclosure will be thorough and complete, It is provided to let you know.
The present invention relates to a copper alloy having a composition of C: not more than 0.10% (excluding 0%), Si: not more than 1.0% (excluding 0%), Mn: not more than 1.0% (excluding 0%), P: , S: not more than 0.020% (excluding 0%), Ni: not more than 2.0% (excluding 0%), Cr: 8.0 to 30%, N: not more than 0.05% A ferritic stainless steel containing an element inevitably included is intended.
In addition, the present invention is characterized by comprising, as wt%, Al: not more than 0.10% (excluding 0%), Mo: not more than 1.0% (excluding 0%), Cu: not more than 1.0% : 0.01 to 0.50%, V: 0.01 to 0.30%, Zr: 0.01 to 0.30%, and B: 0.0010 to 0.0100%.
Carbon (C) is present as an element forming the carbide and is present intrinsically. Therefore, if it is contained excessively, the strength is increased but the impact toughness, corrosion resistance and moldability are lowered. Therefore, the content of C is preferably limited to 0.10% or less .
Silicon (Si) is an important element used as a de-oxidizing material in the production of stainless steel, and it is an element that acts as a ferrite phase stabilizing element while being contained in a certain amount. However, if it is contained in an excessive amount, the precipitation of the intermetallic compound is promoted to lower the elongation, so it is preferable to limit the Si content to 1.0 wt% or less.
Since manganese (Mn) contributes to the formation of inclusions such as MnS when the molten metal is contained excessively in order to improve the fluidity of the molten metal, it is preferable to limit the content of Mn to 1.0 wt% or less .
Since phosphorus (P) and sulfur (S) are added in a very small amount by the manufacturing process or the raw materials in the production of stainless steel and deteriorate hot workability and corrosion resistance, it is preferable to control the content as low as possible. Therefore, the content of P and S is preferably limited to 0.050 wt% or less. Further, a small amount of B can be added to prevent deterioration of hot workability due to segregation of these elements.
Nickel (Ni) is an element which is essentially used for the production of stainless steel. The increase of the Ni content is directly related to the increase of the raw material price, and therefore it is necessary to minimize the amount of Ni, so that the content of Ni is preferably limited to 2.0 wt% or less.
Chromium (Cr) is an element contained for improving the corrosion resistance of stainless steel and has a relatively small influence on the deterioration of hot workability. When the amount of Cr is less than 8.0 wt%, corrosion resistance and oxidation resistance deteriorate. %, There is a problem that the elongation rate is lowered and the cost is increased, so it is preferable to limit the Cr content to 8.0 to 30 wt%.
The amount of nitrogen (N) is preferably 0.05 wt% or less. When the amount of nitrogen (N) exceeds 0.05 wt%, there is a problem that the hot workability is reduced.
It is preferable that Al, Mo, Cu, Ti, Nb, V, Zr, and B are elements which may optionally contain one or more species and are contained in a range satisfying the compositional range defined above.
Aluminum (Al) is an element to be added as a deoxidizer, and when added in a large amount, it causes surface defects, so it is preferable to limit the Al content to 0.10 wt% or less.
The content of molybdenum (Mo) is preferably 1.0 wt% or less. Molybdenum (Mo) is a strong corrosion resistance improving element. When the amount of Mo exceeds 1.0 wt%, there is a problem that workability is lowered.
Copper (Cu) has the advantage of improving the corrosion resistance in a sulfuric acid atmosphere. However, in the chlorine atmosphere, there is a disadvantage that the formal resistance is reduced and the hot workability is lowered, so that the content is preferably limited to 1.0 wt% or less.
The content of titanium (Ti) is preferably 0.01 to 0.50%. If the amount of titanium (Ti) is less than 0.01 wt%, the amount of TiN crystallization is reduced to lower the equiaxed crystal ratio of the slab and increase the number of dissolved C and N elements. On the other hand, There is a problem that the nozzles are clogged when manufacturing the performance slab.
The content of niobium (Nb) is preferably 0.01 wt% or more and 0.50 wt% or less. If the amount of niobium (Nb) is less than 0.01 wt%, there is a problem that the crystal grains become coarse. If the amount is more than 0.05 wt%, the raw material cost rises and the elongation becomes poor due to fine Nb precipitates.
V (vanadium) and zirconium (Zr) are elements added to fix C and N. Particularly, it is an element to be added when the precipitation of Cr carbonitride in the welded portion is suppressed to improve the corrosion resistance and when the high temperature strength is required. However, since it is expensive, each content is preferably limited to 0.01 to 0.30%.
Boron (B) segregates at grain boundaries and strengthens the grain boundaries. However, when added in large amounts, the B content is preferably limited to 0.0010 to 0.0100% because it lowers thermal processability.
Meanwhile, in order to improve the formability of the present invention, molten steel having the above composition is produced by a conventional method to produce a slab, which is then subjected to hot rolling, hot annealing, cold rolling and cold rolling annealing.
The hot rolling, hot annealing, cold rolling and cold annealing described above are carried out by a conventional method for producing a ferritic stainless steel cold rolled steel sheet.
However, hot rolling between hot rolling and cold rolling steps, preferably between hot rolling and hot annealing steps to break coarse crystal grains such as rotated cube assembly texture remaining on the plate after hot rolling, Conduct. By performing hot rolling, the work hardening rate of the plate material is increased, and the coarse crystal grains such as a rotated cube aggregate structure existing in the plate material can be destroyed.
Warm rolling is performed at various rolling rates in the range of 400 to 700 ° C, for example, 10 to 50% reduction.
The reason why the hot rolling is carried out at a temperature in the range of 400 to 700 ° C. is because if the hot rolling temperature is lower than 400 ° C., coarse crystal grains such as rotated cube aggregate do not occur at a desired level, , There is a problem that recrystallization of the structure occurs during warm rolling.
The reason for limiting the rolling reduction to the range of 10 to 50% is that if the rolling reduction is less than 10%, coarse crystal grains such as rotated cube aggregate do not occur at a desired level of fracture, There is a problem that excessive load is generated in the equipment.
[Example]
The following examples illustrate the present invention.
First, the slab having the composition according to the present invention was produced in accordance with the production conditions of commercially produced ferritic stainless steels, and the comparative examples were subjected to hot rolling and hot rolling annealing according to the production conditions of commercially produced ferritic stainless steels. In the examples, hot rolling was carried out according to the production conditions of commercially produced ferritic stainless steels, followed by hot rolling according to the present invention, followed by hot rolling annealing.
The microstructure of the comparative example and the example thus produced were respectively observed with an inverse pole figure (IPF) map. The results of the comparative examples are shown in FIG. 1A, and the results of the examples are shown in FIG. 1B.
In the comparative example of FIG. 1A according to the conventional general process, many coarse crystal grains were observed in the plate material.
On the other hand, in the embodiment of FIG. 1B according to the hot rolling process of the present invention, fine and homogeneous grains are uniformly distributed in all thickness layers, and microstructure and texture are remarkably improved.
The microstructure of the final products obtained by cold rolling and cold rolling annealing according to the production conditions of commercially produced ferritic stainless steels was observed in an inverse pole figure (IPF) map, respectively, and the results of the comparative examples are shown in FIG. And the results of the examples are shown in Fig. 2B.
As can be seen from FIG. 2A, it has been confirmed that pancake-like grains remain in the final cold-rolled annealed material without destroying them according to conventional processes. Rotated cube grains, which adversely affect the formability, were also observed to a considerable extent. (The red grain in the IPF map represents the rotated cube orientation).
On the other hand, as shown in FIG. 2B, when the hot rolling process of the present invention was applied, no pancake-like grains were observed in the final cold-rolled annealed material, and it was confirmed that fine grains were uniformly distributed. It was also confirmed that most of the grains have a high formability orientation. (Blue grain in IPF map means {111} // ND orientation).
Further, as in the comparative example, the r-value of the ferritic stainless steel material subjected only to the hot rolling annealing process, the cold rolling annealing process, and the cold rolling annealing process after the conventional hot rolling process is 1.5 or less, while the hot rolling process is applied after the hot rolling process, , The r-value was found to be 1.6 or more in the ferritic stainless steel material subjected to the hot-rolling annealing, the cold rolling and the cold-rolling annealing process.
Accordingly, it has been confirmed that the hot rolled steel sheet according to the present invention can remarkably improve the formability of the plate material between hot rolling and cold rolling.
Although the present invention has been described with reference to the accompanying drawings and the preferred embodiments described above, the present invention is not limited thereto but is limited by the following claims. Accordingly, those skilled in the art will appreciate that various modifications and changes may be made thereto without departing from the spirit of the following claims.
Claims (5)
Hot rolling the prepared slab;
Hot-rolling the hot-rolled plate at a temperature below the recrystallization temperature of the plate;
Hot rolling the hot rolled plate;
Cold-rolling the hot-rolled sheet material;
A method for manufacturing a ferritic stainless steel excellent in formability, comprising cold rolling and annealing a cold-rolled plate.
Wherein the warm rolling temperature in the step of warm rolling is 400 to 700 占 폚 and excellent in formability.
Wherein the hot rolled steel sheet has excellent hot workability and a reduced rolling reduction rate of 10 to 50%.
The above molten steel contains, by wt%, C: not more than 0.10% (excluding 0%), Si: not more than 1.0% (excluding 0%), Mn: not more than 1.0% , S: not more than 0.020% (excluding 0%), Ni: not more than 2.0% (excluding 0%), Cr: 8.0 to 30%, N: not more than 0.05% A method for producing a ferritic stainless steel excellent in formability including an element inevitably included.
Wherein the molten steel contains, by wt%, Al: not more than 0.10% (excluding 0%), Mo: not more than 1.0% (excluding 0%), Cu: not more than 1.0% (excluding 0%), Ti: 0.01 to 0.50% And at least one element selected from the group consisting of Zr: 0.01 to 0.30%, B: 0.0010 to 0.0100%, and V: 0.01 to 0.30%.
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| KR1020130163591A KR20150075539A (en) | 2013-12-26 | 2013-12-26 | Method for manufacturing ferritic stainless steel sheet with excellent formability |
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| KR1020130163591A KR20150075539A (en) | 2013-12-26 | 2013-12-26 | Method for manufacturing ferritic stainless steel sheet with excellent formability |
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Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN107794356A (en) * | 2016-09-06 | 2018-03-13 | Posco公司 | The manufacture method of the ferrite-group stainless steel of mouldability and the excellent that wrinkles |
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Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN107794356A (en) * | 2016-09-06 | 2018-03-13 | Posco公司 | The manufacture method of the ferrite-group stainless steel of mouldability and the excellent that wrinkles |
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